CN106164017B - Composite sintered body - Google Patents
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- CN106164017B CN106164017B CN201580017546.0A CN201580017546A CN106164017B CN 106164017 B CN106164017 B CN 106164017B CN 201580017546 A CN201580017546 A CN 201580017546A CN 106164017 B CN106164017 B CN 106164017B
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- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B32/00—Carbon; Compounds thereof
- C01B32/25—Diamond
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C3/00—Profiling tools for metal drawing; Combinations of dies and mandrels
- B21C3/02—Dies; Selection of material therefor; Cleaning thereof
- B21C3/025—Dies; Selection of material therefor; Cleaning thereof comprising diamond parts
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- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
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- C04B35/52—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbon, e.g. graphite
- C04B35/528—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbon, e.g. graphite obtained from carbonaceous particles with or without other non-organic components
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- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/64—Burning or sintering processes
- C04B35/645—Pressure sintering
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/38—Non-oxide ceramic constituents or additives
- C04B2235/3817—Carbides
- C04B2235/3826—Silicon carbides
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/42—Non metallic elements added as constituents or additives, e.g. sulfur, phosphor, selenium or tellurium
- C04B2235/422—Carbon
- C04B2235/425—Graphite
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/42—Non metallic elements added as constituents or additives, e.g. sulfur, phosphor, selenium or tellurium
- C04B2235/422—Carbon
- C04B2235/427—Diamond
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/78—Grain sizes and shapes, product microstructures, e.g. acicular grains, equiaxed grains, platelet-structures
- C04B2235/785—Submicron sized grains, i.e. from 0,1 to 1 micron
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/80—Phases present in the sintered or melt-cast ceramic products other than the main phase
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
- C04B2235/9607—Thermal properties, e.g. thermal expansion coefficient
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Abstract
The composite sintered body includes a first phase and a second phase. The first phase is a diamond phase, the second phase is a phase formed using at least one element or compound or both, and the second phase applies strain to the first phase. The content of the second phase is more than 0ppm and not more than 1000 ppm. Thus, a diamond-containing composite sintered body having high wear resistance, high partial wear resistance and high chipping resistance is provided.
Description
Technical Field
The present invention relates to a diamond-containing composite sintered body.
Background
Diamond is a substance having the highest hardness among substances present on the earth, and therefore, a sintered body containing diamond has been used as a material for wear resistant tools, cutting tools, and the like.
Japanese patent laid-open No.2003-292397 (patent document 1) discloses a diamond polycrystal which is a polycrystal composed of diamond obtained by converting and sintering a carbon substance of a graphite-type layered structure at high temperature and high pressure without adding a sintering aid and a catalyst, wherein the diamond has an average particle diameter of 100nm or less and a purity of 99% or more. Japanese patent laid-open No.2003-292397 (patent document 1) also discloses a method of manufacturing diamond polycrystal by direct conversion without adding a sintering aid and a catalyst by placing a non-diamond carbon substance in a pressure unit including an indirect heating means and heating and pressurizing.
International publication No.2009/099130 (patent document 2) discloses a diamond polycrystal obtained by converting and sintering non-diamond carbon under ultrahigh temperature and ultrahigh pressure without adding a sintering aid and a catalyst, in which sintered diamond particles forming the diamond polycrystal have an average particle diameter of more than 50nm and less than 2500nm and a purity of 99% or more, and the particle diameter of D90 of diamond is (average particle diameter + average particle diameter × 0.9) or less.
Japanese patent laying-open No.9-142933 (patent document 3) discloses a diamond sintered body containing 0.1 to 30 vol% of a substance composed of an oxide and/or oxycarbide and/or carbide of a rare earth element, and the balance being diamond.
Japanese patent laid-open No.2005-239472 (patent document 4) discloses a diamond sintered body having high strength and high wear resistance, which contains sintered diamond particles having an average particle diameter of 2 μm or less, and the balance being a binder phase, wherein the content ratio of the sintered diamond particles in the diamond sintered body is 80 vol% or more and 98 vol% or less, and the binder phase contains cobalt and at least one or more elements selected from the group consisting of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium, and molybdenum; the content ratio of cobalt in the binder phase is 50 mass% or more and less than 99.5 mass%; the content ratio of the at least one or more elements in the binder phase is 0.5 mass% or more and less than 50 mass%; and at least one or more elements selected from the group consisting of titanium, zirconium, hafnium, vanadium, niobium, tantalum, chromium and molybdenum are present in the form of carbide particles having an average particle diameter of 0.8 μm or less, the structure of the carbide particles being discontinuous, and adjacent diamond particles being bonded to each other.
Reference list
Patent document
Patent document 1: japanese patent laid-open No.2003-292397
Patent document 2: international publication No.2009/099130
Patent document 3: japanese patent laid-open No.9-142933
Patent document 4: japanese patent laid-open No.2005-239472
Disclosure of Invention
Technical problem
When the diamond polycrystals disclosed in japanese patent laid-open No.2003-292397 (patent document 1) and international patent laid-open No.2009/099130 (patent document 2) are applied to a wire-drawing die as a wear-resistant tool, the pull-out resistance at the time of wire drawing increases, and the wire diameter after wire drawing decreases and wire breakage may be caused to occur frequently due to local wear in the die. When the diamond polycrystal is applied to a water jet (water jet) as a cutting tool, there is a possibility that the service life of the tool may be shortened due to severe abrasion of the nozzle hole portion.
When the diamond sintered bodies disclosed in japanese patent laid-open No.9-142933 (patent document 3) and japanese patent laid-open No.2005-239472 (patent document 4) are applied to a wire drawing die as a wear-resistant tool, the friction coefficient is increased due to metal carbides and metals in the sintered bodies, and thus the wire drawing resistance may be increased, the wire diameter after wire drawing may be reduced, and wire breakage may frequently occur. When the diamond sintered body is applied to a rotary tool, the friction coefficient is increased due to metal carbide and metal in the sintered body, so that cutting resistance may be increased, and tool breakage may occur. When the diamond sintered body is applied to a cutting tool, the friction coefficient increases due to metal carbide and metal in the sintered body, so cutting resistance increases, and excessive vibration occurs and a smooth cutting surface may not be obtained. When the diamond sintered body is applied to an excavating bit, internal destruction occurs due to linear expansion of the metal in the sintered body, thereby possibly shortening the tool life.
The present invention has been made to solve the above problems, and an object thereof is to provide a diamond-containing composite sintered body having high wear resistance, high partial wear resistance, and high chipping resistance.
[ means for solving the problems ]
The composite sintered body of the present invention is a composite sintered body comprising a first phase and a second phase, wherein the first phase is a diamond phase, the second phase is a phase formed of one or more elements or compounds or both, and the second phase applies a strain to the first phase, and the content of the second phase is greater than 0ppm and 1000ppm or less.
Effects of the invention
Since the composite sintered body of the present invention has the above-described constitution, the wear resistance, the partial wear resistance and the chipping resistance are improved.
Detailed Description
Description of embodiments of the invention
First, the outline of the embodiment of the present invention (hereinafter also referred to as "the present embodiment") is described below by listing it as (1) to (5) below.
(1) A composite sintered body according to an embodiment of the present invention is a composite sintered body including a first phase and a second phase, wherein the first phase is a diamond phase, the second phase is a phase formed of one or more elements or compounds or both, and the second phase applies strain to the first phase, and the content of the second phase is greater than 0ppm and 1000ppm or less.
Since the composite sintered body according to the embodiment of the present invention has the above-described configuration, wear resistance, partial wear resistance, and chipping resistance are improved, and occurrence of cracks can be suppressed.
(2) In the composite sintered body according to the present embodiment, the linear expansion coefficient of the second phase is preferably higher than that of the first phase. Thereby, the wear resistance, partial wear resistance and chipping resistance of the composite sintered body are further improved.
(3) In the composite sintered body according to the present embodiment, the average particle diameter of the particles forming the first phase is preferably 1000nm or less. Thereby, the wear resistance, partial wear resistance and chipping resistance of the composite sintered body are further improved.
(4) In the composite sintered body according to the present embodiment, the average particle diameter of the particles forming the second phase is preferably 500nm or less. This further improves the wear resistance, local wear resistance, and chipping resistance of the composite sintered body, and can suppress the occurrence of cracks.
(5) In the composite sintered body according to the present embodiment, the knoop hardness of the composite sintered body is preferably 60GPa or more in order to improve wear resistance.
[ detailed description of embodiments of the invention ]
Although the composite sintered body according to the present embodiment will be described in more detail below, the present embodiment is not limited thereto.
(composite sintered body)
The composite sintered body according to the present embodiment is a composite sintered body including a first phase and a second phase. The first phase is a diamond phase, the second phase is a phase formed from one or more elements or compounds, or both, and the second phase imparts strain to the first phase. The content of the second phase is more than 0ppm and 1000ppm or less.
The above composite sintered body may contain other components such as a sintering aid and a catalyst in addition to the first phase and the second phase.
In the observation of a cross section (an arbitrarily specified cross section, the same applies hereinafter) of the composite sintered body by SEM (scanning electron microscope) or TEM (transmission electron microscope), the presence of a diamond phase was recognized as a bright field, and the presence thereof was confirmed by composition analysis and crystal structure analysis.
The average particle diameter of the particles forming the diamond phase is preferably 1000nm or less, and more preferably 500nm or less, from the viewpoint of improving the local wear resistance and chipping resistance of the composite sintered body. Further, the average particle diameter of the particles forming the diamond phase is 50nm or more, and preferably 200nm or more. Here, the average particle diameter of the particles forming the diamond phase is obtained by: when a cross section of the composite sintered body is observed by SEM or TEM, a photograph is taken under conditions that enable discrimination between the diamond phase, the second phase, and the grain boundary therebetween, followed by image processing (for example, binarization) to calculate an average value of the areas of the respective particles forming the diamond phase, and then the diameter of a circle having the same area as the area is calculated.
In the composite sintered body according to the present embodiment, the second phase is a phase formed of one or more elements or compounds or both, and the second phase applies strain to the first phase. In use of the composite sintered body, the above-mentioned second phase undergoes linear expansion due to frictional heat to apply a compressive stress to the diamond matrix, thereby increasing the hardness of the matrix and reducing wear.
The linear expansion coefficient of the second phase is preferably higher than that of the first phase. Thereby, the effects of increasing the hardness and reducing the wear can be further enhanced. The measurement of the linear expansion coefficient of the second phase was performed by using the following method. First, the composition and crystal structure of the second phase of the composite sintered body were determined by using SEM and TEM methods. Next, a raw material having this composition is separately prepared, and a sintered body including only the second phase is produced by using a desired method. Finally, the obtained sintered body was measured by using the JISR1618 method, thereby obtaining the linear expansion coefficient.
Examples of the above second phase may include SiC, Al, Ti, V, and the like.
In order to prevent cracks and fractures from occurring in the composite sintered body due to excessive expansion of the first phase or the second phase, the content of the second phase in the composite sintered body is 1000ppm or less, and preferably 700ppm or less. In order to reduce friction and wear in the second phase, the content of the second phase in the composite sintered body is more preferably 500ppm or less. Further, in order to apply an appropriate compressive stress to the diamond phase, the content of the second phase is more than 0ppm, preferably 100ppm or more and more preferably 400ppm or more. In the observation of the cross section of the composite sintered body by SEM or TEM, the second phase present in the composite sintered body was recognized as a dark field, and its presence was confirmed by composition analysis and X-ray diffraction.
In order to suppress the occurrence of local cracks in the composite sintered body due to excessive expansion of the first phase or the second phase, the average particle diameter of the particles forming the second phase is preferably 500nm or less. Further, in order to reduce local abrasion in the second phase, the average particle diameter of the particles forming the second phase is preferably 100nm or less. Further, from the viewpoint of improving the structural hardness, the average particle diameter of the particles forming the second phase is 10nm or more, and preferably 50nm or more. Here, the average particle diameter of the particles forming the second phase is obtained by: when a cross section of the composite sintered body is observed by SEM or TEM, a photograph is taken under conditions that enable discrimination between the diamond phase, the second phase, and the grain boundary therebetween, followed by image processing (for example, binarization) to calculate an average value of the areas of the respective particles forming the second phase, and then the diameter of a circle having the same area as the area is calculated.
In order to improve the wear resistance of the composite sintered body, the knoop hardness of the composite sintered body according to the present embodiment is preferably 60GPa or more, and more preferably 80GPa or more. Here, the knoop hardness was measured by using a knoop indenter under a measurement load of 9.8N (1.0 kgf).
[ method of producing composite sintered body ]
The method for producing the composite sintered body according to the present embodiment is not particularly limited. However, in order to manufacture a composite sintered body having high wear resistance, high partial wear resistance, and high chipping resistance in an efficient manner and at low cost, the manufacturing method of the composite sintered body according to the present embodiment preferably includes the steps of:
(a) a raw material preparation step in which a mixture of the raw material non-diamond carbon, the raw material diamond, and the second phase-forming substance, or a mixture of the raw material non-diamond carbon and the second phase-forming substance is prepared.
(b) A composite sintered body forming step of forming a composite sintered body by sintering the aforementioned raw materials under conditions of temperature and pressure at which a diamond phase is formed.
The raw material non-diamond carbon and the raw material diamond prepared in the raw material preparation step are preferably powders in order to form a homogeneous composite sintered body. Further, in order to form a high-quality composite sintered body, the raw material non-diamond carbon is preferably graphite or amorphous carbon.
In the composite sintered body forming step, the sintering conditions are not particularly limited as long as the sintering conditions are temperature and pressure conditions capable of forming a diamond phase. However, in order to efficiently form the diamond phase, the conditions of temperature of 1800 ℃ or more and pressure of 8GPa to 16GPa are preferable, and the conditions of temperature of 2000 ℃ to 2200 ℃ or less and pressure of 11GPa to 14GPa are more preferable. The high temperature and high pressure generating device for generating such high temperature and high pressure is not particularly limited, and examples of the high temperature and high pressure generating device include a band type device, a cube (cubic) type device, a division ball type device, and the like.
Examples
(example 1)
1. Preparation of the raw materials
A mixed powder obtained by adding 400ppm of silicon carbide to graphite powder was prepared as a raw material.
2. Formation of composite sintered body
The mixed powder was sintered for 100 minutes under sintering conditions of a temperature of 2300 ℃ and a pressure of 13GPa using a high-temperature high-pressure generator, thereby obtaining a composite sintered body.
3. Evaluation of Properties of composite sintered body
The diamond phase and the second phase in the composite sintered body were identified and confirmed by SEM observation and X-ray diffraction of one cross section of the composite sintered body, the content of the second phase was calculated from the foregoing SEM observation, the content of the second phase was thus obtained as 300ppm, and the average particle diameter of the particles forming the diamond phase was calculated from the foregoing SEM observation, then, the average particle diameter of the particles forming the diamond phase was 300nm, the average particle diameter of the particles forming the second phase was calculated from the foregoing SEM observation, the average particle diameter of the particles forming the second phase was thus obtained as 60nm, the Knoop hardness of the composite sintered body was measured under a load of 9.8N using a Knoop indenter, the Knoop hardness of the composite sintered body was thus obtained as 75GPa, and further, the linear expansion coefficient of the diamond phase was 1.1 × 10.10-6K, and the linear expansion coefficient of the silicon carbide phase is 6.6 × 10-6/K。
Further, a wire drawing die having an opening size of 20 μm was manufactured using this composite sintered body, and SUS (stainless steel) was drawn at a wire drawing rate of 1000 m/min. The frequency of filament breakage until the opening size of the die was enlarged to 20.5 μm was significantly reduced to one fifth of that in the conventional technique.
Further, the composite sintered body was brazed to a superhard base metal to fabricate a cutting tool having a tip angle of 80 ° and a tip radius of curvature (R) of 80nm, and a nickel plate having a thickness of 20 μm was plated on a 30mm thick copper plate to obtain a nickel-plated metal plate on which grooves having a depth of 5 μm were formed at a pitch of 10 μm. When the wear of the tip of the cutting tool reached 1 μm, the defect state (cracks and chipping) of the tip portion was evaluated by the chipping amount. This results in a significant reduction in the amount of chipping to half that in the conventional technique.
It should be understood that the embodiments and examples disclosed herein are illustrative and are not intended to be limiting in any way. The scope of the invention is indicated by the appended claims rather than by the foregoing description, and is intended to include any modifications within the scope and meaning equivalent to the claims.
Claims (5)
1. A composite sintered body comprising a first phase and a second phase,
the first phase is a diamond phase and,
the second phase is a phase formed of one or more elements or compounds, or both, and the second phase applies strain to the first phase,
the content of the second phase is more than 0ppm and not more than 1000ppm,
the second phase includes SiC.
2. The composite sintered body according to claim 1,
the value of the linear expansion coefficient of the second phase is greater than the value of the linear expansion coefficient of the first phase.
3. The composite sintered body according to claim 1 or 2,
the particles forming the first phase have an average particle diameter of 1000nm or less.
4. The composite sintered body according to claim 1 or 2,
the average particle diameter of the particles forming the second phase is 500nm or less.
5. The composite sintered body according to claim 1 or 2,
the Knoop hardness of the composite sintered body is 60GPa or more.
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
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JP2014093628A JP6390152B2 (en) | 2014-04-30 | 2014-04-30 | Composite sintered body |
JP2014-093628 | 2014-04-30 | ||
PCT/JP2015/057644 WO2015166731A1 (en) | 2014-04-30 | 2015-03-16 | Composite sintered body |
Publications (2)
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CN106164017A CN106164017A (en) | 2016-11-23 |
CN106164017B true CN106164017B (en) | 2020-09-01 |
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CN201580017546.0A Active CN106164017B (en) | 2014-04-30 | 2015-03-16 | Composite sintered body |
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US (1) | US9950960B2 (en) |
EP (1) | EP3138828B1 (en) |
JP (1) | JP6390152B2 (en) |
CN (1) | CN106164017B (en) |
WO (1) | WO2015166731A1 (en) |
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CN111635231B (en) * | 2020-06-05 | 2021-12-17 | 四川大学 | Preparation method of polycrystalline diamond transparent ceramic |
CN111943676B (en) * | 2020-08-10 | 2021-09-21 | 四川大学 | High-impact-strength diamond multiphase material and preparation method thereof |
CN116143518B (en) * | 2021-11-23 | 2024-09-20 | 燕山大学 | Conductive high-strength diamond/amorphous carbon composite material and preparation method thereof |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
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WO1990001986A1 (en) * | 1988-08-17 | 1990-03-08 | The Australian National University | Diamond compact possessing low electrical resistivity |
US5209613A (en) * | 1991-05-17 | 1993-05-11 | Nihon Cement Co. Ltd. | Diamond tool and method of producing the same |
JP2003137653A (en) * | 2001-10-24 | 2003-05-14 | Ishizuka Kenkyusho:Kk | Method of manufacturing composite sintered compact and reaction vessel for the same |
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---|---|---|---|---|
NL281867A (en) | 1961-08-09 | |||
JPS62274034A (en) | 1986-05-23 | 1987-11-28 | Toyota Central Res & Dev Lab Inc | Manufacture of polycrystalline diamond sintered compact by reaction sintering |
CN86104064A (en) | 1986-06-14 | 1987-12-23 | 中国科学院物理研究所 | A kind of composite sintered polycrystalline diamond with inclusion and its production and use |
CN1061918A (en) | 1990-12-05 | 1992-06-17 | 郭朝林 | Powdered carbonide catalysis for synthesizing fine-granularity diamond |
JP3340001B2 (en) | 1995-10-31 | 2002-10-28 | 京セラ株式会社 | Wear-resistant material |
JPH09142933A (en) | 1995-11-21 | 1997-06-03 | Sumitomo Electric Ind Ltd | Diamond sintered compact and its production |
JPH09190873A (en) | 1996-01-05 | 1997-07-22 | Matsushita Electric Ind Co Ltd | Manufacture of sheet heater unit |
EA001843B1 (en) * | 1997-09-05 | 2001-08-27 | Государственное Унитарное Предприятие "Центральный Научно-Исследовательский Институт Материалов" | A method for producing abrasive grains and the abrasive grains produced by this method |
CN1103629C (en) | 1999-11-21 | 2003-03-26 | 张晓� | Clearing agent for synthetizing artificial diamond in conjunction with catalyst and its preparing process |
JP4275896B2 (en) | 2002-04-01 | 2009-06-10 | 株式会社テクノネットワーク四国 | Polycrystalline diamond and method for producing the same |
JP3877677B2 (en) | 2002-12-18 | 2007-02-07 | 独立行政法人科学技術振興機構 | Heat resistant diamond composite sintered body and its manufacturing method |
US7144753B2 (en) | 2003-11-25 | 2006-12-05 | Board Of Trustees Of Michigan State University | Boron-doped nanocrystalline diamond |
WO2005065809A1 (en) | 2003-12-11 | 2005-07-21 | Sumitomo Electric Industries, Ltd. | High-hardness conductive diamond polycrystalline body and method for producing same |
JP4542799B2 (en) | 2004-02-25 | 2010-09-15 | 住友電工ハードメタル株式会社 | High strength and high wear resistance diamond sintered body and method for producing the same |
ATE461013T1 (en) | 2005-08-11 | 2010-04-15 | Element Six Production Pty Ltd | POLYCRYSTALLINE DIAMOND GRINDING ELEMENT AND METHOD FOR THE PRODUCTION THEREOF |
CN2936729Y (en) | 2006-06-09 | 2007-08-22 | 上海江信超硬材料有限公司 | Diamond titanium-chromium alloy nickel composite structure |
CN100506368C (en) | 2006-12-04 | 2009-07-01 | 河南黄河旋风股份有限公司 | Synthesis of conductive diamond |
CN101605918B (en) * | 2007-02-05 | 2012-03-21 | 六号元素(产品)(控股)公司 | Polycrystalline diamond (pcd) materials |
US20080302579A1 (en) | 2007-06-05 | 2008-12-11 | Smith International, Inc. | Polycrystalline diamond cutting elements having improved thermal resistance |
JP5432457B2 (en) | 2008-01-28 | 2014-03-05 | パナソニック株式会社 | Method for producing diamond-like carbon coating |
KR101604730B1 (en) | 2008-02-06 | 2016-03-18 | 스미토모덴키고교가부시키가이샤 | Polycrystalline diamond |
GB0815229D0 (en) | 2008-08-21 | 2008-09-24 | Element Six Production Pty Ltd | Polycrystalline diamond abrasive compact |
JP5534181B2 (en) * | 2010-03-12 | 2014-06-25 | 住友電気工業株式会社 | Diamond polycrystal |
JP5674009B2 (en) * | 2010-09-27 | 2015-02-18 | 住友電気工業株式会社 | High hardness conductive diamond polycrystal and method for producing the same |
JP5672483B2 (en) | 2010-09-27 | 2015-02-18 | 住友電気工業株式会社 | High hardness conductive diamond polycrystal and method for producing the same |
JP2012126605A (en) * | 2010-12-15 | 2012-07-05 | Sumitomo Electric Hardmetal Corp | Diamond sintered compact |
JP2012140256A (en) * | 2010-12-28 | 2012-07-26 | Sumitomo Electric Hardmetal Corp | Diamond sintered compact and method for producing the same |
JP6056431B2 (en) * | 2012-12-06 | 2017-01-11 | 住友電気工業株式会社 | Diamond polycrystals and tools |
-
2014
- 2014-04-30 JP JP2014093628A patent/JP6390152B2/en active Active
-
2015
- 2015-03-16 WO PCT/JP2015/057644 patent/WO2015166731A1/en active Application Filing
- 2015-03-16 CN CN201580017546.0A patent/CN106164017B/en active Active
- 2015-03-16 EP EP15786828.2A patent/EP3138828B1/en active Active
- 2015-03-16 US US15/120,881 patent/US9950960B2/en active Active
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO1990001986A1 (en) * | 1988-08-17 | 1990-03-08 | The Australian National University | Diamond compact possessing low electrical resistivity |
US5209613A (en) * | 1991-05-17 | 1993-05-11 | Nihon Cement Co. Ltd. | Diamond tool and method of producing the same |
JP2003137653A (en) * | 2001-10-24 | 2003-05-14 | Ishizuka Kenkyusho:Kk | Method of manufacturing composite sintered compact and reaction vessel for the same |
Non-Patent Citations (1)
Title |
---|
"惯性技术手册";杨立溪;《惯性技术手册》;中国宇航出版社;20131231;第841页 * |
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JP2015209369A (en) | 2015-11-24 |
WO2015166731A1 (en) | 2015-11-05 |
US9950960B2 (en) | 2018-04-24 |
CN106164017A (en) | 2016-11-23 |
EP3138828A1 (en) | 2017-03-08 |
EP3138828A4 (en) | 2017-12-06 |
EP3138828B1 (en) | 2019-06-12 |
JP6390152B2 (en) | 2018-09-19 |
US20170008807A1 (en) | 2017-01-12 |
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